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EP2460636A1 - Processus comprenant la réticulation du polyéthylène ou son utilisation - Google Patents

Processus comprenant la réticulation du polyéthylène ou son utilisation Download PDF

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Publication number
EP2460636A1
EP2460636A1 EP12156183A EP12156183A EP2460636A1 EP 2460636 A1 EP2460636 A1 EP 2460636A1 EP 12156183 A EP12156183 A EP 12156183A EP 12156183 A EP12156183 A EP 12156183A EP 2460636 A1 EP2460636 A1 EP 2460636A1
Authority
EP
European Patent Office
Prior art keywords
uhmw
sintering
polyethylene
composition
crosslinking
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP12156183A
Other languages
German (de)
English (en)
Inventor
Hans Schmotzer
Yvo Dirix
Paul Smith
Theo Tervoort
Lorenz Brunner
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Smith and Nephew Orthopaedics AG
Original Assignee
Smith and Nephew Orthopaedics AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Smith and Nephew Orthopaedics AG filed Critical Smith and Nephew Orthopaedics AG
Publication of EP2460636A1 publication Critical patent/EP2460636A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C43/00—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor
    • B29C43/003—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor characterised by the choice of material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C43/00—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor
    • B29C43/006—Pressing and sintering powders, granules or fibres
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2023/00—Use of polyalkenes or derivatives thereof as moulding material
    • B29K2023/04—Polymers of ethylene
    • B29K2023/06—PE, i.e. polyethylene
    • B29K2023/0658—PE, i.e. polyethylene characterised by its molecular weight
    • B29K2023/0683—UHMWPE, i.e. ultra high molecular weight polyethylene
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29L—INDEXING SCHEME ASSOCIATED WITH SUBCLASS B29C, RELATING TO PARTICULAR ARTICLES
    • B29L2031/00—Other particular articles
    • B29L2031/753—Medical equipment; Accessories therefor
    • B29L2031/7532—Artificial members, protheses

Definitions

  • the present invention relates to processes comprising crosslinking polyethylene or using crosslinked polyethylene, and to products obtained therewith.
  • Ultrahigh molecular weight polyethylene (UHMW PE) is well known for, among other properties, its chemical resistance, low friction coefficient, high toughness, and resistance against wear. As a result, it has found numerous applications in demanding environments where some or all of the above properties are required. Equally well known is the intractability of this polymer, which is due to the fact that UHMW PE above its crystalline melting temperature, does not form a fluid phase that is of a viscosity that permits melt-processing techniques used with common thermoplastic polymers.
  • a process comprising:
  • a process comprising:
  • processes comprising crosslinking polyethylene or processes using crosslinked polyethylene.
  • the processes further involve compacting polyethylene and/or sintering polyethylene.
  • the polyethylenes used in the present invention are substantially linear polymers of ethylene.
  • the polyethylene has a value of the weight-average molecular weight (M w ) of more than 1,000,000 g/mol, for instance more than 1,500,000, more than 2,000,000 g/mol, more than 3,000,000 g/mol, more than 4,000,000 g/mol, more than 5,000,000 g/mol, more than 6,000,000 g/mol, more than 7,000,000 g/mol, and even more than 10,000,000 g/mol.
  • M w weight-average molecular weight
  • the weight average molecular weight is below 20,000,000 g/mol, e.g. below 15,000,000 g/mol, below 10,000,000 g/mol, or below 8,000,000 g/mol.
  • the polydispersity (the ratio between the weight- and number average molecular weight) of the polyethylenes may vary. In an embodiment, the polydispersity is more than 1, for instance more than 2, more than 2.5, or more than 3. In an embodiment, the polydispersity is less than 100, for instance less than 75, less than 50, less than 20, less than 15, or less than 10.
  • the polyethylene has a melting temperature of at least 105°C, for instance at least 115°C, at least 125°C, or at least 135°C.
  • melting temperature is the peak melting temperature of the polyethylene as determined in differential scanning calorimetry at a heating rate of 10°C/min, after first melting the polyethylene and recrystallizing it at a cooling rate of 10°C/min).
  • the UHMW PE grades for use in the present invention can be synthesized according to conventional methods for the polymerization of ethylene as described in detail in the literature (for example, Whiteley, K. S., in Industrial Polymers Handbook, Wilkes, E. S. ed., Wiley-VCH, Volume 2, pp. 643-691, 2001 ) and as practiced in the art. Many UHMW PE grades are products of commerce, and may be used in the present invention.
  • the present invention employs compositions comprising at least 35wt% UHMW PE, relative to the total weight of the composition.
  • the compositions comprise at least 50wt%, at least 65wt%, at least 75wt%, at least 90 wt%, at least 95wt%, or at least 99 wt% UHMW PE.
  • the compositions consist essentially of UHMW PE.
  • the polyethylenes are "virgin” polymers.
  • the term “virgin” is intended to mean that the polymer has not been molten or fully dissolved since its manufacture. Use of virgin polymers may assist in ease of processing when compared with non-virgin polymers. For instance, previously processed, e.g. sintered, UHMW PE would typically have an increased entanglement density when compared with virgin UHMW PE.
  • the polyethylene is medical grade UHMWPE, as described by ASTM standards ASTM D4020, F648-00, F2003-00, F2102-01 and F2183-02, and ISO standards ISO 11542.1/.2 and 5834.1/.2.
  • the (composition comprising) polyethylene is compacted to form an object (e.g. a block) of compacted polyethylene.
  • object e.g. a block
  • Compacting prior to further processing e.g. sintering, may assist in providing a relatively better wear, impact strength, and/or fatigue crack growth resistance when compared with further processing without compacting.
  • the manner of compacting may vary and depend, e.g., on the size of the object to be formed.
  • the compacting is effected at elevated temperatures and pressures (the temperature remains below the melting temperature of the polyethylene, however).
  • the compacting is effected by filling a mold with polyethylene and placing the mold in a press that is at a temperature below the melting temperature of the polyethylene.
  • the compacting temperature is at least 30°C, for instance at least 60°C, at least 80°C, at least 100°C, at least 110°C, at least 120°C, or at least 125°C. In an embodiment, the temperature is below 135°C, e.g. below 125°C, below 120°C, below 110°C, or below 100°C. In an embodiment, the temperature is about 120°C.
  • pressure is applied to the mold.
  • the pressure may be a single pressure or the pressure may be varied. For instance, an initial pressure of, e.g., at least 5MPa, for instance at least 10MPa, at least 15 MPa, or at least 20 MPa is applied, and held for a certain period of time (e.g.
  • compacting is performed under shear.
  • Compacting under shear generally enhances plastic deformation of the particles and may therewith improve particle contact.
  • compacting under shear is performed by solid-state extrusion, e.g. sheet extrusion, or rolling.
  • compacting is performed in an air atmosphere. In an embodiment, compacting is performed in an inert atmosphere, e.g. an argon or nitrogen atmosphere.
  • compacting is performed in a reactive atmosphere, e.g. in an atmosphere comprising (effective amounts of) hydrogen, acetylene (ethyn), ethene, and/or propene.
  • a reactive atmosphere e.g. in an atmosphere comprising (effective amounts of) hydrogen, acetylene (ethyn), ethene, and/or propene.
  • additives are added to the polyethylene prior to compacting.
  • the additives include radical scavengers, for instance vitamine E, vitamin A, vitamin C, phenolic antioxidants (e.g. BHT (E321, 2,6 ditertiarybutyl-4-methyl-phenol)), irganox 1010, carotenes (such as beta carotene), or mixtures thereof.
  • radical scavengers for instance vitamine E, vitamin A, vitamin C, phenolic antioxidants (e.g. BHT (E321, 2,6 ditertiarybutyl-4-methyl-phenol)), irganox 1010, carotenes (such as beta carotene), or mixtures thereof.
  • the (composition comprising) UHMW PE is sintered.
  • the composition/polyethylene is compacted before sintering.
  • the manner of sintering may vary and may depend, e.g., on the shape and size of the object to be sintered.
  • the temperatures at which the sintering is carried out are above the melting temperature of the polyethylene, but preferably below temperatures at which substantial degradation of the polymer may occur.
  • the sintering temperature is more than about 2°C above the polyethylene melting temperature, for instance more than about 5°C, more than about 10°C, more than about 20°C, more than about 30°C, more than about 40°C, or more than about 50°C.
  • polyolefins may display signs of degradation at temperatures well above 200°C.
  • sintering is preferably carried out at temperatures below 250°C, for instance below 230°C, below 210°C or below 190°C.
  • the time for completion of the sintering process may vary widely, and is dependent on, among other things, the size and shape of the object and the efficiency of heat transfer.
  • the sintering occurs in an inert atmosphere, e.g. an argon or a nitrogen atmosphere.
  • the compacted polyethylene is sintered under pressure.
  • the pressure applied during the sintering process may vary and depend, e.g., on the shape and dimensions of the object.
  • the pressure is at least 5 MPa, e.g. at least 10 MPa, at least 20 MPa, or at least 40 MPa. In an embodiment, the pressure is less than 500 MPa.
  • a process is provided wherein the polyethylene is subjected only once to a temperature above its melting temperature.
  • sintering is performed in a reactive atmosphere, e.g. in an atmosphere comprising (effective amounts of) hydrogen, acetylene (ethyn), ethene, and/or propene.
  • the present processes comprise crosslinking polyethylene or using crosslinked polyethylene.
  • Crosslinking may assist in further improving the wear resistance of the UHMW PE.
  • the crosslinking is initiated below the melting temperature of the UHMW PE.
  • the crosslinking is initiated after compacting but before sintering.
  • the crosslinking is initiated after compacting and during sintering (i.e. in the melt).
  • the crosslinking is initiated after compacting and after sintering (i.e. after or during cooling down from the melt).
  • Crosslinking may be initiated, e.g., with reactive additives, with gamma radiation, with electron beam radiation, or combinations thereof.
  • the crosslinking is initiated with gamma radiation.
  • the dose may vary and depend, e.g., on the size of the object and on whether a certain degree of polymer degradation would be acceptable.
  • the dose is at least 1 MRad, e.g. at least 4 MRad, at least 7 MRad, at least 10 MRad, at least 12 MRad, or at least 15 MRad.
  • the dose is at most 50 MRad, e.g. at most 35 MRad, at most 25 MRad, or at most 15 MRad.
  • the crosslinking is initiated with gamma radiation. In an embodiment, the crosslinking is initiated with electron beam radiation.
  • the dose may vary and depend, e.g., on the size of the object and on whether a certain degree of polymer degradation would be acceptable.
  • the dose is at least 1 MRad, e.g. at least 4 MRad, at least 7 MRad, at least 10 MRad, at least 12 MRad, or at least 15 MRad.
  • the dose is at most 50 MRad, e.g. at most 35 MRad, at most 25 MRad, at most 15 MRad, at most 10 MRad, or at most 8 MRad.
  • the energy of the electron beam may vary and be, e.g., at least 100 keV, such as at least 500 keV, at least 1MeV, at least 4 MeV, or at least 7 MeV. In an embodiment, the energy is below 20 MeV.
  • crosslinking is initiated more than once, e.g. 2 times or 3 times. In an embodiment, crosslinking is initiated during compacting and again initiated during sintering. In an embodiment, crosslinking is initiated during sintering and again during cooling. In an embodiment, crosslinking is initiated during compacting, again initiated during sintering, and again initiated during cooling. In an embodiment, the initiation of crosslinking is at increasing dose. For instance, in an embodiment, the first time the dose of radiation is in the range of 1-4 Mrad and the second time the dose is between 4-7 Mrad.
  • products include biomedical intermediates or products such as artificial implants, for instance orthopedic implants, e.g. parts of an artificial hip, of an artificial knee, of an artificial shoulder, of an artificial toe, of an artificial elbow, or an artificial ankle.
  • Other examples include, e.g., products where the polyethylene forms part or the whole of an automotive part, an outdoor product, a composite material, a mono- or multi-filament fiber, an oriented or un-oriented fiber, a woven or non-woven fabric, a filter, a membrane, a film, a multi-layer- and/or multicomponent film, a barrier film, a container, a bag, a bottle, a rod, a liner, a vessel, a pipe, a valve, an O-ring, a gasket, ski soles, snow board soles, snow mobile runners, sliding parts (e.g.
  • Charpy impact strength was determined on rectangular (120x15x10 mm), double notched test specimens prepared according to ISO 11542-2. All Charpy impact tests were performed on a Zwick 5113E pendulum impact tester according to ISO 179-1.
  • CT compact tension
  • F ( ⁇ ) is a geometric factor and ⁇ corresponds to a/W.
  • ⁇ K th was calculated by determining the best-fit straight line from a linear regression of log da / dN versus log ⁇ K between the lowest detected growth rate and the onset of the log da / dN , log ⁇ K proportionality (in most cases between growth rates of 10 -6 and 10 -5 mm/cycle). Generally, a higher ⁇ K th value can be related to a higher required stress intensity factor (or load amplitude) to initiate crack inception. All experiments were performed at room temperature.
  • Abrasive wear measurements were carried out using a custom-built device according to specifications and method analogous to those described by Hutchings [ Trezona, R. I., Allsopp, D. N., Hutchings, I. M., Wear, 229, 205 (1999 )].
  • the sample (circular with a diameter of 20mm; thickness 0.6mm) was placed against the ball with a normal force of 0.27 N, while an abrasive slurry (0.75 g SiC (mean particle size of 4-5 microns) per cm 3 distilled water) was dripping onto the ball at a feed rate of 5 cm 3 /min.
  • GUR 4020 was sintered, and the charpy impact of the sintered GUR 4020 was determined to be 191 kJ/M 2 .
  • Example 1 was repeated, except that GUR 4020 was compacted before sintering.
  • the charpy impact of the compacted and sintered GUR 4020 was determined to be 202 kJ/M 2 .
  • GUR 1020 was sintered, and the fatigue crack growth resistance of the sintered GUR 1020 was determined to be 1.25 MPa/m 1/2 .
  • Example 3 was repeated, except that GUR 1020 was compacted before sintering.
  • the fatigue crack growth resistance of the compacted and sintered GUR 1020 was determined to be 1.32 MPa/m 1/2 .
  • Example 5 was repeated, except that all samples were compacted before sintering.
  • the wear coefficient of these samples was determined and is shown as squares in Figure 2 .
  • Samples of GUR 4020 were compacted.
  • the compacted samples were irradiated at room temperature with gamma rays or with electrons (10 MeV) at room temperature.
  • the dose of gamma radiation that the samples received differed among the samples and ranged from 0 to 15 MRad.
  • Samples that instead received electron (e-beam) radiation all received a dose of 7 MRad.
  • the samples were sintered and their Charpy impact strength was determined. The results are shown in Figure 3 , with the gamma irradiated samples indicated as closed triangles ( ⁇ ) and the e-beam sample as an open triangle ( ⁇ ).
  • Samples of GUR 1020 were compacted and subsequently sintered.
  • the thus obtained samples were irradiated with E-beam at 125°C and at a dose of 7MRad, followed by thermal treatment for 9 hours at 150°C (which is above the melting temperature of GUR 1020). After these 9 hours, the samples were allowed to cool down to room temperature.
  • the fatigue crack growth resistance of the thus obtained samples was determined to be 0.92 MPa/m 1 ⁇ 2 .
  • Example 8 was repeated, except that the compaction was omitted.
  • the fatigue crack growth resistance of the thus obtained samples was determined to be 0.84 MPa/m 1 ⁇ 2 .
  • Samples of GUR 1020 were compacted.
  • the compacted samples were sintered, and during sintering the samples were irradiated with E-beam at a dose of 7MRad.
  • the crosslinking was initiated after compaction but during sintering (melt irradiation).
  • the fatigue crack growth resistance of the thus obtained samples was determined to be 0.89 MPa/m 1 ⁇ 2 .

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials For Medical Uses (AREA)
  • Compositions Of Macromolecular Compounds (AREA)
  • Processes Of Treating Macromolecular Substances (AREA)
  • Prostheses (AREA)
  • Treatments Of Macromolecular Shaped Articles (AREA)
EP12156183A 2006-10-30 2006-10-30 Processus comprenant la réticulation du polyéthylène ou son utilisation Withdrawn EP2460636A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP06818318.5A EP2083981B1 (fr) 2006-10-30 2006-10-30 Procédés qui comprennent la réticulation de polyéthylène ou l'utilisation du polyéthylène réticulé
PCT/EP2006/010423 WO2008052574A1 (fr) 2006-10-30 2006-10-30 Procédés qui comprennent la réticulation de polyéthylène ou l'utilisation du polyéthylène réticulé

Related Parent Applications (2)

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EP06818318.5A Division-Into EP2083981B1 (fr) 2006-10-30 2006-10-30 Procédés qui comprennent la réticulation de polyéthylène ou l'utilisation du polyéthylène réticulé
EP06818318.5 Division 2006-10-30

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EP2460636A1 true EP2460636A1 (fr) 2012-06-06

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EP12156183A Withdrawn EP2460636A1 (fr) 2006-10-30 2006-10-30 Processus comprenant la réticulation du polyéthylène ou son utilisation
EP06818318.5A Active EP2083981B1 (fr) 2006-10-30 2006-10-30 Procédés qui comprennent la réticulation de polyéthylène ou l'utilisation du polyéthylène réticulé

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US (1) US8871131B2 (fr)
EP (2) EP2460636A1 (fr)
JP (1) JP2010508405A (fr)
CN (1) CN101616782A (fr)
AU (2) AU2006350369A1 (fr)
CA (1) CA2669386A1 (fr)
WO (1) WO2008052574A1 (fr)

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US8871131B2 (en) 2014-10-28
JP2010508405A (ja) 2010-03-18
AU2013205914A1 (en) 2013-06-06
WO2008052574A1 (fr) 2008-05-08
AU2006350369A1 (en) 2008-05-08
EP2083981B1 (fr) 2021-10-06
CA2669386A1 (fr) 2008-05-08
AU2013205914B2 (en) 2015-05-07
US20100069576A1 (en) 2010-03-18
CN101616782A (zh) 2009-12-30

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